EP3135787B1 - Stahlplatte und verfahren zur herstellung davon - Google Patents

Stahlplatte und verfahren zur herstellung davon Download PDF

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Publication number
EP3135787B1
EP3135787B1 EP15783445.8A EP15783445A EP3135787B1 EP 3135787 B1 EP3135787 B1 EP 3135787B1 EP 15783445 A EP15783445 A EP 15783445A EP 3135787 B1 EP3135787 B1 EP 3135787B1
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Prior art keywords
steel plate
less
content
temperature
toughness
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English (en)
French (fr)
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EP3135787A4 (de
EP3135787A1 (de
Inventor
Shigeki KITSUYA
Katsuyuki Ichimiya
Kazukuni Hase
Shigeru Endo
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JFE Steel Corp
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JFE Steel Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
    • B21B1/26—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B2001/225—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by hot-rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present disclosure relates to a steel plate that is suitable for use in steel structures such as buildings, bridges, ships, offshore structures, construction machinery, tanks, and penstocks, and to a method of producing the steel plate.
  • steel materials are welded in accordance with shapes of steel structures in order to form desired shapes.
  • there has been remarkable development in the production of larger scale steel structures and thus there has been significant progress toward higher strength and thicker steel materials used to produce such steel structures.
  • the large thickness of the steel plate causes the thickness central part to experience a lower cooling rate, which facilitates formation of a microstructure such as ferrite that has relatively low strength. Consequently, it is necessary to add large amounts of alloying elements in order to inhibit formation of such a microstructure.
  • NPL 1 describes a steel plate having a plate thickness of 210 mm
  • NPL 2 describes a steel plate having a plate thickness of 180 mm.
  • PL 1 constitutes prior art under Article 54(3) EPC and relates to a thick high-toughness high-strength steel plate which has a specific chemical composition and includes a microstructure having, throughout an entire region in the plate thickness direction, an average prior austenite grain size of not more than 50 ⁇ m and a martensite and/or bainite phase area fraction of not less than 80%.
  • a continuously cast slab having the specific chemical composition is heated to 1200°C to 1350°C, hot worked with a strain rate of not more than 3/s and a cumulative working reduction of not less than 15%, and thereafter hot rolled and heat treated.
  • the steel plate has a mixed structure of a martensite phase in which an average circle-equivalent diameter of former austenite grains is 30-100 ⁇ m and an average aspect ratio is 4 or less, and a bainite phase.
  • the manufacturing method includes hot-rolling the steel having the above composition, then rapidly cooling the plate and reheating the plate.
  • PL 3 relates to a method for providing superior toughness at low temperature to a steel by performing a plate rolling-hardening process for a B-added low alloy steel slab under specific conditions, and then exerting tempering.
  • the plate rolling - direct hardening treatment process for a slab of a B-added low alloy steel the surface and the rear surface of the steel slab after roughing is water-cooled, and the steel slab is sequentially subjected to finish rolling while recuperating a surface layer part, to direct hardening, and then to tempering.
  • PL 4 relates to a high strength, low yield ratio steel material with 40 mm or less sheet thickness, which has a tensile strength of 590 MPa or more and a low yield ratio of 80% or less and is suitable for steel structures.
  • the steel material has a specific chemical composition and has a microstructure composed of polygonal ferrite with a mean circle-equivalent diameter of 3-20 ⁇ m and an area fraction of 5-30%, and bainite or martensite.
  • PL 1 EP 2 942 414 A1
  • PL 2 JP 5 354 164 B2
  • PL 3 JP 2 913 426 B2
  • PL 4 JP 5 477 457 B2
  • the inventors presume that the phenomenon described above occurs due to a shear-type reverse transformation. Specifically, nucleation and growth of ⁇ grains normally occur from prior ⁇ grain boundaries during heating of a steel material, and refinement and homogenization of prior ⁇ grain size occur in association therewith. However, in a situation in which large amounts of alloying elements are contained in the steel material, nucleation and growth of ⁇ grains are less likely to occur as described above and a shear-type reverse transformation may occur in which the prior ⁇ grains themselves undergo a sudden reverse transformation to austenite. Consequently, ⁇ grains remain coarse in a part of the steel material in which this reverse transformation occurs. Moreover, bainite and martensite obtained by cooling from this state are also coarse.
  • NPL 1 and 2 cited above do not describe a technique that could resolve the difficulty of refining prior ⁇ grain size during heat treatment. Therefore, a technical problem remains from a viewpoint of reliably producing steel plates that have excellent strength and toughness in a mid-thickness part thereof.
  • an objective of the present disclosure is to provide a steel plate that has excellent strength and toughness in a mid-thickness part thereof, despite having a plate thickness of 100 mm or greater, and to provide a method of producing this steel plate.
  • the inventors conducted diligent research directed toward steel plates having a yield strength of 620 MPa or greater and a plate thickness of 100 mm or greater.
  • the inventors' research focused on factors that can be used to control internal microstructure of a steel plate in order to obtain excellent strength and toughness in a mid-thickness part of the steel plate.
  • the inventors reached the following findings as a result of their research.
  • the present disclosure is based on the findings described above and has the following primary features.
  • a steel plate can be obtained that has excellent strength and toughness in a mid-thickness part thereof, and thus has excellent strength and toughness throughout the steel, despite having a plate thickness of 100 mm or greater. Therefore, the present disclosure makes a significant contribution to increasing the scale and improving the safety of steel structures and has a considerable effect in industry.
  • C is a useful element for cheaply obtaining the strength that is required for structural-use steel. Accordingly, C content is set as 0.08% or greater. On the other hand, C content of greater than 0.20% causes noticeable deterioration in steel plate and heat-affected zone toughness. Accordingly, the C content is set as 0.20% or less. The C content is preferably from 0.08% to 0.14%.
  • Si is added for the purpose of deoxidation, but causes noticeable deterioration in steel plate and heat-affected zone toughness if Si content is greater than 0.40%. Accordingly, the Si content is set as 0.40% or less.
  • the Si content is from 0.05% to 0.40% and preferably from 0.10% to 0.30%.
  • Mn is added from a viewpoint of ensuring steel plate strength and toughness, but this effect is not sufficiently obtained when Mn content is less than 0.5%.
  • Mn content of greater than 5.0% not only causes deterioration of steel plate toughness, but also promotes central segregation and increases the scale of slab porosity. Accordingly, the Mn content is set as 5.0% or less.
  • the Mn content is preferably from 0.6% to 2.0% and more preferably from 0.6% to 1.6%.
  • P content of greater than 0.015% causes noticeable deterioration in steel plate and heat-affected zone toughness. Accordingly, the P content is limited to 0.015% or less. However, it is not essential that P is contained in the chemical composition.
  • S content of greater than 0.0050% causes noticeable deterioration in steel plate and heat-affected zone toughness. Accordingly, the S content is limited to 0.0050% or less. However, it is not essential that S is contained in the chemical composition.
  • Cr is an effective element for increasing steel plate strength, but reduces weldability if added in a large amount. Accordingly, Cr content is set as 3.0% or less. The Cr content is preferably from 0.1% to 2.0%. However, it is not essential that Cr is contained in the chemical composition.
  • Ni 5.0% or less (inclusive of 0%)
  • Ni is a beneficial element for improving steel plate strength and heat-affected zone toughness.
  • Ni content of greater than 5.0% has a noticeable negative effect on cost efficiency. Accordingly, the Ni content is set as 5.0% or less.
  • the Ni content is preferably from 0.5% to 4.0%. However, it is not essential that Ni is contained in the chemical composition.
  • Al 0.080% or less (inclusive of 0%)
  • Al is added in order to sufficiently deoxidize molten steel.
  • Al content of greater than 0.080% increases the amount of dissolved Al in the steel plate and reduces steel plate toughness. Accordingly, the Al content is set as 0.080% or less.
  • the Al content is preferably from 0.030% to 0.080% and more preferably from 0.030% to 0.060%. However, it is not essential that Al is contained in the chemical composition.
  • N has an effect of improving steel plate and heat-affected zone toughness by refining microstructure through formation of nitrides with Ti and the like.
  • N content of greater than 0.0070% increases the amount of dissolved N in the steel plate, noticeably reduces steel plate toughness, and further reduces heat-affected zone toughness by also forming coarse carbonitrides in the heat-affected zone. Accordingly, the N content is set as 0.0070% or less.
  • the N content is from 0.0010% to preferably 0.0050% and more preferably from 0.0010% to 0.0040%.
  • B has an effect of increasing quench hardenability by segregating at austenite grain boundaries to inhibit ferrite transformation from the grain boundaries.
  • B content of greater than 0.0030% reduces quench hardenability due to precipitation of B as a carbonitride, and consequently reduces toughness. Accordingly, the B content is set as 0.0030% or less.
  • the B content is from 0.0003% to 0.0030% and preferably from 0.0005% to 0.0020%.
  • O content of greater than 0.0025% causes formation of hard oxides in the steel plate and noticeably reduces toughness. Accordingly, the O content is set as 0.0025% or less. The O content is preferably from 0% to 0.0020%.
  • a steel plate according to one embodiment of the present disclosure is composed of the basic elements described above, with the balance being Fe and incidental impurities.
  • the chemical composition may further contain one or more selected from Cu, Mo, V, and Ti with an objective of increasing strength and toughness.
  • Cu is a useful element for improving steel plate strength without reducing toughness, but causes cracks to occur in the surface of the steel plate during hot working if Cu content is greater than 0.50%. Accordingly, the Cu content is preferably 0.50% or less in a situation in which Cu is added.
  • Mo is an effective element for increasing steel plate strength, but increases hardness due to alloy carbide precipitation and reduces toughness if Mo content is greater than 1.50%. Accordingly, the Mo content is preferably 1.50% or less in a situation in which Mo is added. The Mo content is more preferably from 0.020% to 0.80%.
  • V 0.200% or less
  • V has an effect of improving steel plate strength and toughness and effectively lowers the amount of dissolved N by precipitating as VN.
  • V content of greater than 0.200% reduces toughness due to precipitation of hard VC.
  • the V content is preferably 0.200% or less in a situation in which V is added.
  • the V content is more preferably from 0.010% to 0.100%.
  • Ti forms TiN during heating, effectively inhibits coarsening of austenite, and improves steel plate and heat-affected zone toughness.
  • Ti content of greater than 0.020% causes coarsening of Ti nitrides and reduces steel plate toughness. Accordingly, Ti content is preferably in a range of from 0.005% to 0.020% in a situation in which Ti is added. The Ti content is more preferably from 0.008% to 0.015%.
  • the chemical composition may further contain one or more selected from Mg, Ta, Zr, Y, Ca, and REMs with an objective of further enhancing material properties.
  • Mg forms a stable oxide at high temperature, effectively inhibits coarsening of prior ⁇ grains in a heat-affected zone, and is an effective element for improving weld toughness, but these effects are poorly obtained if Mg content is less than 0.0001%.
  • Mg content of greater than 0.002% increases the amount of inclusions and reduces toughness. Accordingly, the Mg content is preferably from 0.0001% to 0.002% in a situation in which Mg is added.
  • the Mg content is more preferably from 0.0001% to 0.015%.
  • Ta 0.01% to 0.20%
  • Ta effectively improves strength when added, but this effect is poorly obtained if Ta content is less than 0.01%.
  • Ta content of greater than 0.20% reduces toughness due to precipitate formation. Accordingly, the Ta content is preferably from 0.01% to 0.20% in a situation in which Ta is added.
  • Zr is an effective element for improving steel plate strength, but this effect is poorly obtained if Zr content is less than 0.005%.
  • Zr content of greater than 0.1% causes formation of a coarse precipitate and reduces toughness. Accordingly, the Zr content is preferably from 0.005% to 0.1% in a situation in which Zr is added.
  • Y forms a stable oxide at high temperature, effectively inhibits coarsening of prior ⁇ grains in a heat-affected zone, and is an effective element for improving weld toughness, but these effects are poorly obtained if Y content is less than 0.001%.
  • Y content of greater than 0.01% increases the amount of inclusions and reduces toughness. Therefore, Y content is preferably from 0.001% to 0.01% in a situation in which Y is added.
  • Ca is a useful element for morphological control of sulfide inclusions.
  • Ca content is set as 0.0005% or greater in order to display this effect.
  • Ca content of greater than 0.0050% leads to a reduction in cleanliness and deterioration of toughness.
  • the Ca content is preferably from 0.0005% to 0.0050% in a situation in which Ca is added.
  • the Ca content is more preferably from 0.0005% to 0.0025%.
  • REMs have an effect of enhancing material properties by forming oxides and sulfides in the steel plate in the same way as Ca.
  • REM content is set as 0.0005% or greater in order to obtain this effect. However, this effect reaches saturation if REM content is greater than 0.0100%. Accordingly, the REM content is preferably from 0.0005% to 0.0100% in a situation in which REMs are added. The REM content is more preferably from 0.0005% to 0.0050%.
  • the subject of the present disclosure is a type of steel for which the shear-type reverse transformation described above tends to readily occur and for which it is difficult to refine and homogenize prior ⁇ grain size.
  • the aforementioned type of steel can be classified by the equivalent carbon content thereof and excellent effects can be displayed when an equivalent carbon content Ceq IIW of the chemical composition defined by the following formula (1) is 0.65% or greater.
  • the subject of the present disclosure is a steel plate having a chemical composition that in addition to containing the basic components in the content ranges described above, has an equivalent carbon content Ceq IIW of 0.65% or greater.
  • Ceq IIW % C + % Mn / 6 + % Cu + % Ni / 15 + % Cr + % Mo + % V / 5 ⁇ 0.65
  • [%M] indicates the content (mass%) of an element M in the steel plate and has a value of 0 in a situation in which the element is not contained in the steel plate.
  • the phrase "the element is not contained” refers to a situation in which the content of the element cannot be determined because the content is smaller than the detectable limit.
  • the equivalent carbon content Ceq IIW is calculated using the following formula (1') instead of the previously provided formula (1) in a situation in which in which the optional additive components Cu, Mo, and V are not added.
  • Ceq IIW % C + % Mn / 6 + % Ni / 15 + % Cr / 5 ⁇ 0.65
  • Toughness has a strong correlation with prior ⁇ grain size and tends to decrease with increasing prior ⁇ grain size.
  • a desired level of toughness can be reliably ensured through prior ⁇ grain size in a mid-thickness part having a maximum value, expressed as an equivalent circle diameter, of 150 ⁇ m or less.
  • the maximum value of prior ⁇ grain size in the mid-thickness part is preferably 120 ⁇ m or less.
  • mid-thickness part refers to a region at a depth of from 45% to 55% of the plate thickness from the surface of the steel plate in a plate thickness direction (i.e., a region located centrally in the plate thickness direction and extending for 10% of the plate thickness). It should be noted that conventional techniques are not expected to enable reduction of the maximum value of prior ⁇ grain size in the mid-thickness part to 150 ⁇ m or less.
  • prior ⁇ grain size in surface layer parts of the steel plate which are regions extending for 5% of the plate thickness in the plate thickness direction from opposite surfaces of the steel plate
  • prior ⁇ grain size in the surface layer parts inevitably has a maximum value of 150 ⁇ m or less when prior ⁇ grain size in the mid-thickness part has a maximum value of 150 ⁇ m or less.
  • the microstructure is a martensite and/or bainite microstructure.
  • the remainder of the microstructure is ferrite, pearlite, or the like.
  • the "total area ratio of martensite and bainite in the mid-thickness part" is determined by inspecting the microstructure of a sample taken from the mid-thickness part. Specifically, the total area ratio is determined through observation under a scanning electron microscope for at least 50 observation fields at ⁇ 3000 magnification and through quantification of the microstructure.
  • the steel plate has excellent strength and toughness in the mid-thickness part thereof, despite having a plate thickness of 100 mm or greater. Specifically, it is possible to achieve a yield strength of 620 MPa or greater and a steel plate toughness at -40°C (vE -40°C ) of 170 J or greater. Alternatively, it is possible to achieve a yield strength of 690 MPa or greater and a steel plate toughness at -40°C (vE -40°C ) of 100 J or greater. Although no specific upper limit is set for the plate thickness, the plate thickness is for example 300 mm or less in the case of a normal steel plate.
  • temperatures (°C) described herein refer to the temperature of the mid-thickness part.
  • Molten steel adjusted to the chemical composition described above is produced by a normal steel making method such as using a converter, an electric heating furnace, or a vacuum melting furnace, and the molten steel is subsequently cast by a normal casting method such as continuous casting or ingot casting to obtain a semi-finished casting product for rolling, such as a slab or a billet.
  • a normal steel making method such as using a converter, an electric heating furnace, or a vacuum melting furnace
  • a normal casting method such as continuous casting or ingot casting to obtain a semi-finished casting product for rolling, such as a slab or a billet.
  • blooming may be performed in order to reduce the plate thickness of the semi-finished casting product.
  • Heating temperature of semi-finished casting product Ac 3 temperature to 1200°C
  • the semi-finished casting product is heated to at least the Ac 3 temperature and no higher than 1200°C. Heating of the semi-finished casting product to at least the Ac 3 transformation temperature is performed in order to homogenize the steel as a single austenite phase. Specifically, the heating temperature is preferably at least 1000°C and no higher than 1200°C.
  • [%M] indicates the content (mass%) of an element M in the semi-finished casting product.
  • the semi-finished casting product is hot rolled to obtain a steel plate having a plate thickness of 100 mm or greater.
  • the composition to which the present disclosure is directed which is a composition for which refinement and homogenization of prior ⁇ grain size do not readily occur during heat treatment, it is important that formation of coarse prior ⁇ grains during hot rolling is inhibited. Promotion of recrystallization in ⁇ regions, and in particular recrystallization in a latter part of rolling, is particularly effective for refining prior ⁇ grains.
  • a steel plate having a plate thickness of 100 mm or greater is to be produced, it is difficult to perform sufficient working by hot rolling.
  • At least five passes of hot rolling are performed, and more preferably at least six passes and no more than eleven passes of hot rolling are performed.
  • recrystallization in a mid-thickness part can be effectively promoted and formation of coarse prior ⁇ grains can be inhibited by performing each of at least three of the last five passes with a rolling reduction of 8% or greater.
  • Three or four passes of hot rolling may be performed in a situation in which constraints due to the semi-finished casting product make it difficult to perform five or more passes of hot rolling.
  • recrystallization in the mid-thickness part can be effectively promoted and formation of coarse prior ⁇ grains can be inhibited by performing at least one pass with a rolling reduction of 8% or greater and at least one other pass with a rolling reduction of 15% or greater.
  • the steel plate is allowed to cool to a temperature of 300°C or lower, is subsequently reheated to at least the Ac 3 temperature and no higher than 1050°C, and is subsequently rapidly cooled to 350°C or lower from a temperature at least as high as an Ar 3 temperature.
  • the reason that the reheating temperature is no higher than 1050°C is that reheating the steel plate to a high temperature that is higher than 1050°C causes austenite grain coarsening and noticeably reduces steel plate toughness.
  • a reheating temperature lower than the Ar 3 temperature also leads to reduced steel plate toughness.
  • the reason that the cooling stop temperature is 350°C or lower is that if the cooling stop temperature is higher than 350°C, steel plate toughness deteriorates due to non-uniform formation of carbides during a subsequent air cooling step and formation of coarse carbides during tempering.
  • [%M] indicates the content (mass%) of an element M in the semi-finished casting product.
  • the temperature of the mid-thickness part is determined by simulation calculation or the like based on plate thickness, surface temperature, cooling conditions, and so forth.
  • the temperature of the mid-thickness part may be determined by calculating a temperature distribution in the plate thickness direction by the finite difference method.
  • the method of rapid cooling is normally water cooling.
  • a cooling method other than water cooling such as gas cooling or the like, may be adopted because the cooling rate is preferably as fast as possible.
  • the tempering temperature is set as at least 450°C and no higher than 700°C.
  • a tempering temperature of lower than 450°C leads to reduced toughness due to the influence of low temperature tempering embrittlement, whereas a tempering temperature of higher than 700°C causes precipitation of various carbides and leads to coarsening of steel plate microstructure and reduced strength.
  • quenching is sometimes repeated with an objective of steel toughening. In the same way, quenching may also be repeated in the present disclosure.
  • a final repetition of quenching is preferably performed with rapid cooling to 350°C or lower after heating to at least the Ac 3 temperature and no higher than 1050°C, and subsequent tempering is preferably performed at 450°C to 700°C.
  • Steels having the chemical compositions of steels 1-29 in Table 1 (note that the balance was Fe and incidental impurities) were produced by steel making, and continuously-cast slabs having slab thicknesses shown in Table 2 were produced from these steels.
  • Each of the slabs was hot rolled under conditions shown in Table 2 to form a steel plate having a plate thickness shown in Table 2.
  • each of the steel plates was subjected to heat treatment (quenching-tempering processes) under conditions shown in Table 2.
  • the steel plates obtained as final products were tested as follows.

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Claims (2)

  1. Stahlplatte, aufweisend;
    eine chemische Zusammensetzung, die, in Massen%, aus
    0,08% bis 0,20% C;
    0,05% bis 0,40% Si;
    0,5% bis 5,0% Mn;
    0,015% oder weniger P;
    0,0050% oder weniger S;
    0% bis 3,0% Cr;
    0% bis 5,0% Ni;
    0% bis 0,080% Al;
    0,0010% bis 0,0070% N;
    0,0003% bis 0,0030% B;
    0% bis 0,0025% O, und optional einem oder mehreren ausgewählt aus
    0,50% oder weniger Cu;
    1,50% oder weniger Mo;
    0,200% oder weniger V;
    0,005% bis 0,020% Ti;
    0,0001% bis 0,002% Mg;
    0,01% bis 0,20% Ta;
    0,005% bis 0,1% Zr;
    0,001% bis 0,01% Y;
    0,0005% bis 0,0050% Ca; und
    0,0005% bis 0,0100% REMs
    und als Rest aus Fe und zufälligen Verunreinigungen besteht, wobei
    die chemische Zusammensetzung einem nachfolgend gezeigtem Zusammenhang (1) genügt, Ceq IIW = % C + % Mn / 6 + % Cu + % Ni / 15 + % Cr + % Mo + % V / 5 ≥ 0,65
    Figure imgb0011
    wobei [%M] den Gehalt eines Elementes M in der Stahlplatte in Massen% bezeichnet und in einer Situation, in der das Element M nicht in der Stahlplatte enthalten ist, den Wert 0 annimmt,
    ein Gefüge, in dem:
    die vorherige γ-Korngröße in einem Abschnitt der Stahlplatte mittlerer Dicke einen Maximalwert von 150 µm oder weniger, ausgedrückt als ein äquivalenter Kreisdurchmesser, aufweist; und
    ein Gesamtflächenanteil von Martensit und Bainit in dem Abschnitt mittlerer Dicke 80% oder mehr beträgt, und
    eine Streckfestigkeit von 620 MPa oder mehr und eine Plattendicke von 100 mm bis 300 mm.
  2. Verfahren zur Herstellung der Stahlplatte gemäß Anspruch 1, umfassend:
    Aufheizen eines Halbzeug-Gusserzeugnisses, das die chemische Zusammensetzung von Anspruch 1 aufweist, auf zumindest eine Ac3-Temperatur und nicht höher als 1200°C;
    anschließend Unterwerfen des Halbzeug-Gusserzeugnisses einem Warmwalzen mit drei oder mehr Stichen, um eine Stahlplatte zu erhalten, die eine Plattendicke von 100 mm oder größer aufweist;
    anschließend Abkühlen der Stahlplatte auf 300°C oder niedriger;
    anschließend Wiederaufheizen der Stahlplatte auf zumindest die Ac3-Temperatur und nicht höher als 1050°C;
    anschließend schnelles Abkühlen der Stahlplatte mittels Wasserkühlen oder Gaskühlen auf 350°C oder niedriger von einer Temperatur entsprechend einer oder höher als eine Ar3-Temperatur; und
    anschließend Unterwerfen der Stahlplatte einem Temperprozess bei einer Temperatur von zumindest 450°C und nicht höher als 700°C, wobei
    in einer Situation, in der das Warmwalzen aus drei oder vier Stichen besteht, zumindest ein Stich mit einer Walzreduktion von 8% oder größer durchgeführt wird und zumindest ein weiterer Stich mit einer Walzreduktion von 15% oder größer durchgeführt wird, und in einer Situation, in der das Warmwalzen aus fünf oder mehr Stichen besteht, zumindest drei der letzten fünf Stiche jeweils mit einer Walzreduktion von 8% oder größer durchgeführt werden.
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CA2945439C (en) 2020-03-10
EP3135787A4 (de) 2017-03-01
WO2015162939A8 (ja) 2016-10-06
JPWO2015162939A1 (ja) 2017-04-13
CN106232850A (zh) 2016-12-14
CA2945439A1 (en) 2015-10-29
JP5871109B1 (ja) 2016-03-01
US20170044639A1 (en) 2017-02-16
KR101892839B1 (ko) 2018-08-28
SG11201608464UA (en) 2016-11-29
EP3135787A1 (de) 2017-03-01
KR20160143732A (ko) 2016-12-14
WO2015162939A1 (ja) 2015-10-29
US10358688B2 (en) 2019-07-23

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